CN113906588A

CN113906588A - Modified silicon particles for silicon-carbon composite electrodes

Info

Publication number: CN113906588A
Application number: CN202080040863.5A
Authority: CN
Inventors: 伊恩·拉塞尔·布朗; 季立文; 拉胡尔·R·卡马斯; 莫妮卡·奇霍恩
Original assignee: Enevate Corp
Current assignee: Enevate Corp
Priority date: 2019-06-03
Filing date: 2020-06-03
Publication date: 2022-01-07
Also published as: EP3977543A1; US11548991B2; KR20220016495A; US20210163699A1; WO2020247527A1; US11028242B2; US20200377678A1; EP3977543A4

Abstract

A method of forming a composite film can include providing a mixture including a precursor and silane-treated silicon particles. The method may also include pyrolyzing the mixture to convert the precursor to one or more carbon phases to form the composite film, wherein the silicon particles are distributed throughout the composite film.

Description

Modified silicon particles for silicon-carbon composite electrodes

Technical Field

The present application relates generally to silicon particles. In particular, the present application relates to silicon particles for battery electrodes and composites comprising silicon particles.

Background

Lithium ion batteries typically include a separator and/or an electrolyte between an anode and a cathode. In one type of cell, the separator, cathode and anode materials are formed into sheets or films, respectively. Sheets of the cathode, separator, and anode are stacked or rolled in sequence such that the separator separates the cathode from the anode (e.g., electrodes) to form a battery. Typical electrodes include a layer of electrochemically active material on a conductive metal (e.g., aluminum and copper). The film may be rolled or cut into pieces, which are then stacked into a stack. The stack has alternating electrochemically active materials and separators therebetween.

Disclosure of Invention

In certain embodiments, methods of forming composite films are disclosed. The method can include providing a mixture including a precursor and silane treated silicon particles. The method may further include pyrolyzing the mixture to convert the precursor into one or more carbon phases to form the composite film, wherein the silicon particles are distributed throughout the composite film.

In various embodiments, the silane-treated silicon particles may comprise silicon particles treated with one or more organosilanes. For example, silane treated silicon particles may include a silicon oxide surface that reacts with one or more organosilanes. In some cases, the one or more organosilanes may include one or more silanols, silyl ethers, silyl chlorides, dialkylaminosilanes, silyl hydrides, or cyclic azasilanes.

In some methods, the one or more organosilanes may comprise one or more aminoalkyl-functional groups. For example, the one or more organosilanes may include 3-aminopropyltriethoxysilane, N- (2-aminoethyl) -3-aminopropyltrimethoxysilane, or 2, 2-dimethoxy-1, 6-diaza-2-silacyclooctane. In some cases, the precursor may include polyimide.

In some methods, the one or more organosilanes may comprise an epoxide linker. For example, the epoxide linker may include 5, 6-epoxyhexyltriethoxysilane. In some cases, the precursor may include a phenolic resin.

In some methods, the one or more organosilanes may comprise aromatic functional groups. For example, the one or more organosilanes may include benzyltriethoxysilane. In some cases, the precursor can include a polycyclic aromatic hydrocarbon.

In some methods, the one or more organosilanes may include dodecyl silane.

In some methods, the one or more organosilanes may include (N, N-dimethylamino) trimethylsilane.

In some methods, the silicon particles may be suspended in a liquid comprising one or more organosilanes.

In some methods, the silicon particles may be exposed to one or more organosilane vapors.

In some methods, the mixture can include one or more organosilanes.

In some embodiments, the composite film may comprise from about 50 wt% to about 99 wt% silicon particles. The composite film may be electrochemically active. The one or more types of carbon phases may be continuous phases that maintain the composite film.

In various embodiments, methods of forming battery electrodes are disclosed. The electrode may comprise a composite film as described herein. In some cases, the electrode may be an anode.

Drawings

FIG. 1A illustrates an embodiment of a method of forming a composite material, including forming a mixture comprising a precursor, casting the mixture, drying the mixture, curing the mixture, and pyrolyzing the precursor;

FIG. 1B is a schematic representation of the formation of silicon carbide on silicon particles;

FIGS. 2A and 2B are SEM micrographs of one embodiment of micron-sized silicon particles milled from larger silicon particles;

FIGS. 2C and 2D are SEM micrographs of one embodiment of micron-sized silicon particles with nano-sized features on the surface;

FIG. 2E illustrates an exemplary embodiment of a method of forming a composite material;

FIG. 3A schematically illustrates an exemplary silane treated silicon particle;

FIG. 3B illustrates an exemplary embodiment of a method of forming a composite material;

FIG. 4 is a graph of discharge capacity at an average rate of C/2.6;

FIG. 5 is a graph of discharge capacity at an average rate of C/3;

FIG. 6 is a graph of discharge capacity at an average rate of C/3.3;

FIG. 7 is a graph of discharge capacity at an average rate of C/5;

FIG. 8 is a graph of discharge capacity at an average rate of C/9;

fig. 9 is a graph of discharge capacity;

FIG. 10 is a graph of discharge capacity at an average rate of C/9;

11A and 11B are graphs of reversible capacity and irreversible capacity as a function of respective weight percentages of PI-derived carbon and graphite particles from 2611c for a fixed percentage of 20 wt.% Si;

FIG. 12 is a graph of first cycle discharge capacity as a function of weight percent carbon;

FIG. 13 is a graph of reversible (discharge) capacity and irreversible capacity as a function of pyrolysis temperature;

FIG. 14 is a photograph of a 4.3cm by 4.3cm composite anodic film without a metal foil support layer;

FIG. 15 is a Scanning Electron Microscope (SEM) micrograph of the composite anodic film prior to cycling (the out-of-focus portion is the bottom portion of the anode and the in-focus portion is the cleaved edge of the composite film);

FIG. 16 is another SEM micrograph of a composite anodic membrane prior to cycling;

FIG. 17 is an SEM micrograph of a composite anodic film after 10 cycles;

FIG. 18 is another SEM micrograph of a composite anodic film after 10 cycles;

FIG. 19 is an SEM micrograph of a composite anodic film after 300 cycles;

FIG. 20 includes an SEM micrograph of a cross section of a composite anodic film;

FIG. 21 is an X-ray powder diffraction (XRD) pattern of sample silicon particles;

FIG. 22 is an SEM micrograph of one embodiment of silicon particles;

FIG. 23 is another SEM micrograph of one embodiment of silicon particles;

FIG. 24 is an SEM micrograph of one embodiment of silicon particles;

FIG. 25 is an SEM micrograph of one embodiment of silicon particles;

FIG. 26 is a chemical analysis of sample silicon particles;

FIGS. 27A and 27B are exemplary particle size histograms for two micron-sized silicon particles with nanometer-sized features;

fig. 28 is a graph comparing the discharge capacity of two types of exemplary silicon particles during battery cycling;

FIG. 29 shows X-ray photoelectron spectroscopy (XPS) spectra of exemplary silane treated silicon particles and untreated silicon particles;

FIG. 30A is a scanning electron microscope (SEM-FIB) photomicrograph with a focused ion beam of a cross-section of an exemplary silicon-carbon composite made with untreated silicon particles;

FIG. 30B is an SEM-FIB micrograph of a cross section of an exemplary silicon-carbon composite made with silane-treated silicon particles;

fig. 31 shows a graph of capacity retention versus cycle number for a full cell comprising silane treated silicon particles compared to a full cell comprising untreated silicon particles; and

fig. 32 shows a plot of capacity retention versus cycle number for full cells containing silane treated silicon particles compared to full cells containing untreated silicon particles in subsequent experiments.

Detailed Description

The silicon-carbon composite electrode may include silicon particles suspended in a carbon matrix. The electrode may comprise a composite material as a self-supporting structure or attached to a current collector. Silicon-carbon electrodes can provide superior energy density compared to industry standard graphite electrodes. The silicon-carbon electrode may also have superior cycle life and initial coulombic efficiency compared to a silicon electrode consisting of silicon particles, conductive additives, and a polymer binder.

In some embodiments for fabricating a silicon composite electrode, silicon particles may be suspended in an organic thermoplastic or thermoset binder and formed into a self-supporting film, which may then be thermally treated to convert the organic material into carbon. The carbon matrix may serve as a conductive structural component that may hold the electrodes together. In some such designs, it may be beneficial for the carbon to be in intimate contact with the silicon particles. To achieve such intimate contact, it may be helpful to both wet (e.g., substantially wet or fully wet in some cases) the silicon particles with the carbon precursor (e.g., to achieve increased and/or maximum interfacial contact), and to have the precursor adhere strongly to the silicon particles. Without being bound by theory, if the silicon particles are not wetted by the carbon precursor, voids and/or pores may appear at the interface between the silicon and the carbon, which may adversely affect the strength and conductivity of the composite.

As described herein, in some embodiments, silicon particles with tailored surface chemistries can be used to improve wetting by matching surface energy to the carbon precursor, and strong adhesion can be promoted by providing reactive sites on the silicon particle surface to achieve one or more bonding interactions (e.g., pi stacking, dipole-dipole interactions, hydrogen bonding, and/or covalent bonding) with the carbon precursor.

A typical carbon anode electrode includes a current collector such as a copper sheet. Carbon is deposited on the collector along with an inactive binder material. Carbon is commonly used because carbon has excellent electrochemical properties and is also electrically conductive. If the current collector layer (e.g., copper layer) is removed, the carbon may not be able to mechanically support itself. Thus, conventional electrodes require a support structure such as a collector to be able to function as an electrode. The electrode (e.g., anode or cathode) combinations described in this application can result in self-supporting electrodes. The need for a metal foil current collector is eliminated or minimized as the conductive carbonized polymer is used for current collection in the anode structure as well as for mechanical support. In typical applications in the mobile industry, metal current collectors are often added to ensure adequate rate capability. In contrast to particulate carbon suspended in a non-conductive binder in one type of conventional lithium ion battery electrode, the carbonized polymer may form a substantially continuous conductive carbon phase throughout the electrode. Advantages of carbon composite blends employing carbonized polymers may include, for example, 1) higher capacity, 2) enhanced overcharge/discharge protection, 3) lower irreversible capacity due to elimination (or minimization) of metal foil current collectors, and 4) potential cost savings due to simpler manufacturing.

Anode electrodes currently used in rechargeable lithium ion batteries typically have a specific capacity (including metal foil current collectors, conductive additives, and binder materials) of about 200 milliamp hours per gram. The active material graphite used in most lithium ion battery anodes has a theoretical energy density of 372 milliampere hours per gram (mAh/g). In contrast, silicon has a high theoretical capacity of 4200 mAh/g. In order to increase the volumetric and gravimetric energy densities of lithium ion batteries, silicon may be used as the active material for the cathode or anode. Various types of silicon materials (e.g., silicon nanopowders, silicon nanowires, porous silicon, and ball-milled silicon) have also been reported as viable candidates for the active material of the negative or positive electrode. Small particle sizes (e.g., in the nanometer range) can generally increase cycle life performance. They can also exhibit very high irreversible capacity. However, small particle sizes may also result in very low volumetric energy densities (e.g., for the entire battery stack) due to the difficulty of encapsulating the active material. Larger particle sizes (e.g., micron or micron range sizes) can generally result in higher density anode materials. However, the expansion of the silicon active material may result in poor cycle life due to particle breakage. For example, silicon may expand by more than 300% upon lithium intercalation. Due to this expansion, the anode comprising silicon should allow for expansion while maintaining electrical contact between the silicon particles.

As described herein and in U.S. patent application No. 13/008,800 (U.S. patent No. 9,178,208) and U.S. patent application No. 13/601,976 (U.S. patent application publication No. 2014/0170498), entitled "Composite Materials for Electrochemical Storage" and "Silicon Particles for Battery Electrodes," respectively, the entire contents of which are hereby incorporated by reference, certain embodiments employ a method of producing a monolithic, self-supporting anode using a carbonized polymer. Because the polymer is converted to a conductive and electrochemically active matrix, the resulting electrode is sufficiently conductive that a metal foil or mesh current collector can be omitted or minimized. The converted polymer also acts as a buffer for the expansion of the silicon particles during cycling, so that a high cycle life can be achieved. In certain embodiments, the resulting electrode is an electrode consisting essentially of an active material. In other embodiments, the resulting electrode is substantially an active material. The electrode may have a high energy density of about 500mAh/g to about 3500mAh/g, which may be attributed to, for example, 1) the use of silicon, 2) the elimination or substantial reduction of metal current collectors, and 3) being composed entirely or substantially entirely of active material.

As described in U.S. patent application No. 14/821,586 entitled "Surface Modification of Silicon Particles for Electrochemical Storage" (U.S. patent application publication No. 2017/0040598), the entire contents of which are hereby incorporated by reference, in certain embodiments, the carbonized polymer may react with a native Silicon oxide Surface layer on the Silicon Particles. In some embodiments, the surface of the particles is modified to form a surface coating thereon that may further act as a swelling buffer for the silicon particles during cycling. The surface coating may comprise silicon carbide.

The composite materials described herein can be used as anodes in most conventional lithium ion batteries; they may also be used as cathodes in some electrochemical couples with additional additives. The composite material may also be used in secondary batteries (e.g., rechargeable) or primary batteries (e.g., non-rechargeable). In certain embodiments, the composite material is a self-supporting structure. In other embodiments, the composite material is a self-supporting monolithic structure. For example, the collector may be included in an electrode composed of a composite material. In certain embodiments, the composite material may be used to form Carbon Structures discussed in U.S. patent application No. 12/838,368 (U.S. patent application publication No. 2011/0020701), entitled "Carbon Electrode Structures for Batteries," the entire contents of which are hereby incorporated by reference. Further, the composite materials described herein may be, for example, silicon composites, carbon composites, and/or silicon-carbon composites. Certain embodiments may further include a composite material comprising micron-sized Silicon Particles, as described in U.S. patent application No. 13/799,405 (U.S. patent No. 9,553,303), entitled "Silicon Particles for Battery Electrodes," the entire contents of which are hereby incorporated by reference. For example, in some embodiments, micron-sized silicon particles have nanometer-sized features on the surface. Silicon particles having such geometries may have both the benefits of micron-sized silicon particles (e.g., high energy density) and the benefits of nano-sized silicon particles (e.g., good cycling behavior). As used herein, the term "silicon particles" may generally include micron-sized silicon particles with or without nanometer-sized features.

Some composite materials may be provided on a current collector. In some embodiments, the composite material may be attached to the current collector using an attachment substance. The attachment substance and current collector may be any of those known in the art or yet to be developed. For example, some composite materials may be provided on a current collector as described in U.S. patent application No. 13/333,864 (U.S. patent No. 9,397,338) entitled "Electrodes, Electrochemical Cells, and Methods of Forming Electrodes and Electrochemical Cells" or U.S. patent application No. 13/796,922 (U.S. patent No. 9,583,757) entitled "Electrodes, Electrochemical Cells, and Methods of Forming Electrodes and Electrochemical Cells," each of which is incorporated herein by reference. Some anodes may be formed on a Current Collector, for example, as described in U.S. patent application No. 15/471,860 entitled "Methods of Forming Carbon-Silicon Composite Material a Current Collector" (U.S. patent application publication No. 2018/0287129), which is incorporated herein by reference.

FIG. 1A illustrates one embodiment of a method 100 of forming a composite material. For example, a method of forming a composite material may include forming a mixture including a precursor, block 101. The method may further comprise pyrolyzing the precursor to convert the precursor to a carbon phase. The precursor mixture may contain carbon additives such as graphite active materials, chopped or milled carbon fibers, carbon nanofibers, carbon nanotubes, and/or other carbons. After the precursor is pyrolyzed, the resulting carbon material may be a self-supporting monolithic structure. In certain embodiments, one or more materials are added to the mixture to form a composite material. For example, silicon particles may be added to the mixture. Carbonizing the precursor creates an electrochemically active structure that holds the composite together. For example, the carbonized precursor may be a substantially continuous phase. Silicon particles including micron-sized silicon particles with or without nano-sized features may be distributed throughout the composite material. Advantageously, the carbonized precursor may be a structural material as well as an electrochemically active and electrically conductive material. In certain embodiments, the material particles added to the mixture are uniformly or substantially uniformly distributed throughout the composite material to form a uniform or substantially uniform composite.

The mixture may comprise a plurality of different components. The mixture may comprise one or more precursors. In certain embodiments, the precursor is a hydrocarbon compound. For example, the precursor may include polyamideimide, polyamic acid, polyimide, and the like. Other precursors may include phenolic resins, epoxy resins, and/or other polymers. The mixture may also comprise a solvent. For example, the solvent may be N-methyl-pyrrolidone (NMP). Other possible solvents include acetone, diethyl ether, gamma-butyrolactone, isopropanol, dimethyl carbonate, ethyl carbonate, dimethoxyethane, ethanol, methanol, and the like. Examples of precursor and solvent solutions include PI-2611(HD Microsystems), PI-5878G (HD Microsystems), and VTEC PI-1388(RBI, Inc.). PI-2611 consists of > 60% n-methyl-2-pyrrolidone and 10% to 30% s-biphenyl dianhydride/p-phenylenediamine. PI-5878G consists of > 60% n-methylpyrrolidone, 10% to 30% polyamic acid of pyromellitic dianhydride/oxydianiline, 10% to 30% aromatic hydrocarbon (petroleum distillate) containing 5% to 10% 1,2, 4-trimethylbenzene. In certain embodiments, the amount of precursor in the solvent is from about 10% to about 30% by weight. Additional materials may also be included in the mixture. For example, as previously discussed, silicon particles or carbon particles including graphite active materials, chopped or milled carbon fibers, carbon nanofibers, carbon nanotubes, graphite, and other conductive carbons may be added to the mixture. In addition, the mixture may be mixed to homogenize the mixture.

In certain embodiments, the mixture is cast onto a substrate, block 102 in fig. 1A. In some embodiments, casting comprises using gap extrusion, tape casting, or blade casting techniques. Blade casting techniques may include applying a coating to a substrate by using a flat surface (e.g., a blade) that is controlled a distance above the substrate. A liquid or slurry may be applied to the substrate and the blade may be passed over the liquid to spread the liquid over the substrate. Since the liquid passes through the gap between the blade and the substrate, the thickness of the coating can be controlled by the gap between the blade and the substrate. Excess liquid may also be scraped off as it passes through the gap. For example, the mixture may be cast onto a substrate comprising a polymer sheet, a polymer roll, and/or a foil or roll made of glass or metal. The mixture may then be dried to remove the solvent, block 103. For example, the polyamic acid and NMP solution may be dried at about 110 ℃ for about 2 hoursTo remove the NMP solution. The dried mixture may then be removed from the substrate. For example, the aluminum substrate can be etched away with HCl. Alternatively, the dried mixture may be removed by peeling the dried mixture from the substrate or otherwise mechanically removing the dried mixture from the substrate. In some embodiments, the substrate comprises polyethylene terephthalate (PET), including for example

In certain embodiments, the dried mixture is a film or sheet. In some embodiments, the dried mixture is optionally cured, block 104. In some embodiments, the dried mixture may be further dried. For example, the dried mixture may be placed in a hot press (e.g., between graphite plates in an oven). A hot press may be used to further dry and/or cure and keep the dried mixture flat. For example, the dried mixture from the polyamic acid and NMP solution can be hot pressed at about 200 ℃ for about 8 to 16 hours. Alternatively, the entire process including casting and drying can be accomplished in a roll-to-roll process using standard film processing equipment. The dried mixture may be rinsed to remove any solvent or etchant that may remain. For example, Deionized (DI) water may be used to rinse the dried mixture. In certain embodiments, tape casting techniques may be used for casting. In some embodiments, the mixture may be coated on the substrate by a slot die coating process (e.g., metering a constant or substantially constant weight and/or volume by a set or substantially set gap). In some other embodiments, there is no substrate for casting, and the anodic film need not be removed from any substrate. The dried mixture may be cut or mechanically divided into smaller parts.

The mixture is further subjected to pyrolysis to convert the polymer precursor to carbon, block 105. In certain embodiments, the mixture is pyrolyzed in a reducing atmosphere. For example, an inert atmosphere, vacuum and/or flowing argon, nitrogen or helium may be used. In some embodiments, the mixture is heated to about 900 ℃ to about 1350 ℃. For example, a polyimide formed from a polyamic acid can be carbonized at about 1175 ℃ for about one hour. In certain embodiments, the heating rate and/or cooling rate of the mixture is about 10 ℃/min. A retainer may be used to hold the mixture in a particular geometry. The holder may be graphite, metal, or the like. In certain embodiments, the mixture is maintained flat. After the mixture is pyrolyzed, tabs (tab) may be attached to the pyrolyzed material to form electrical contacts. For example, nickel, copper, or alloys thereof may be used for the tabs.

In certain embodiments, one or more of the methods described herein can be performed in a continuous process. In certain embodiments, casting, drying, possible curing, and pyrolysis may be performed in a continuous process. For example, the mixture may be coated onto a glass or metal roller. The mixture may be dried while rotating on a drum to produce a film. The film may be transferred or peeled as a roll and fed into another machine for other processing. Extrusion and other film making techniques known in the industry may also be employed prior to the pyrolysis step.

Pyrolysis of the precursor produces a carbon material (e.g., at least one carbon phase). In certain embodiments, the carbon material is hard carbon. In some embodiments, the precursor is any material that can be pyrolyzed to form hard carbon. When the mixture contains one or more additional materials or phases in addition to the carbonized precursor, a composite material may be produced. In particular, the mixture may comprise silicon particles that result in a silicon-carbon composite (e.g., at least one first phase comprising silicon and at least one second phase comprising carbon) or a silicon-carbon composite (e.g., at least one first phase comprising silicon, at least one second phase comprising carbon, and at least one third phase comprising carbon).

The silicon particles can increase the lithium intercalation specific capacity (specific lithium intercalation capacity) of the composite material. As silicon absorbs lithium ions, it undergoes a substantial volume increase on the order of 300+ volume percent, which can cause electrode structural integrity problems. In addition to the volume expansion related problems, silicon is not inherently conductive, but becomes conductive when it is alloyed (e.g., lithiated) with lithium. When silicon is delithiated, the surface of the silicon loses conductivity. Furthermore, when silicon is delithiated, the volume decreases, which leads to the possibility that the silicon particles lose contact with the matrix. The significant change in volume also leads to mechanical failure of the silicon particle structure, which in turn causes it to shatter. The pulverization and loss of electrical contact make the use of silicon as an active material in lithium ion batteries challenging. The reduction in the initial size of the silicon particles can prevent further pulverization of the silicon powder and minimize the loss of surface conductivity. Furthermore, adding a material to the composite that can elastically deform as the volume of the silicon particles changes can reduce the chance that electrical contact to the silicon surface is lost. For example, the composite material may contain carbon, such as graphite, which aids in the ability of the composite to absorb expansion, and also to intercalate lithium ions to increase the storage capacity of the electrode (e.g., chemically active). Thus, the composite material may comprise one or more types of carbon phases.

In some embodiments, the particle size (e.g., the diameter or largest dimension of the silicon particles) may be less than about 50 μm, less than about 40 μm, less than about 30 μm, less than about 20 μm, less than about 10 μm, less than about 1 μm, about 10nm to about 50 μm, about 10nm to about 40 μm, about 10nm to about 30 μm, about 10nm to about 20 μm, about 0.1 μm to about 20 μm, about 0.5 μm to about 20 μm, about 1 μm to about 15 μm, about 1 μm to about 10 μm, about 10nm to about 1 μm, less than about 500nm, less than about 100nm, and the like. All, substantially all, or at least some of the silicon particles may include the particle sizes (e.g., diameters or largest dimensions) described above. For example, the average particle size (e.g., average diameter or average largest dimension) or median particle size (or median diameter or median largest dimension) of the silicon particles can be less than about 50 μm, less than about 40 μm, less than about 30 μm, less than about 20 μm, less than about 10 μm, less than about 1 μm, about 10nm to about 50 μm, about 10nm to about 40 μm, about 10nm to about 30 μm, about 10nm to about 20 μm, about 0.1 μm to about 20 μm, about 0.5 μm to about 20 μm, about 1 μm to about 15 μm, about 1 μm to about 10 μm, about 10nm to about 1 μm, less than about 500nm, less than about 100nm, and the like. In some embodiments, the silicon particles may have a distribution of particle sizes. For example, at least about 95%, at least about 90%, at least about 85%, at least about 80%, at least about 70%, or at least about 60% of the particles can have a particle size as described herein.

The amount of silicon provided in the mixture or in the composite material may be greater than 0% by weight of the mixture and/or composite material. In certain embodiments, the amount of silicon may be from about 0 wt% to about 99 wt% of the composite, including from greater than about 0 wt% to about 99 wt%, from greater than about 0 wt% to about 95 wt%, from greater than about 0 wt% to about 90 wt%, from greater than about 0 wt% to about 35 wt%, from greater than about 0 wt% to about 25 wt%, from about 10 wt% to about 35 wt%, at least about 30 wt%, from about 30 wt% to about 99 wt%, from about 30 wt% to about 95 wt%, from about 30 wt% to about 90 wt%, from about 30 wt% to about 80 wt%, at least about 50 wt%, from about 50 wt% to about 99 wt%, from about 50 wt% to about 95 wt%, from about 50 wt% to about 90 wt%, from about 50 wt% to about 80 wt%, from about 50 wt% to about 70 wt%, at least about 60 wt%, from about 60 wt% to about 99 wt%, from about 0 wt% to about 90 wt%, from about 35 wt%, from about 0 wt% to about 25 wt%, from about 10 wt% to about 35 wt%, from about 30 wt%, from about 80 wt%, from about 30 wt% to about 90 wt%, from about 90 wt% of the composite, From about 60 wt% to about 95 wt%, from about 60 wt% to about 90 wt%, from about 60 wt% to about 80 wt%, at least about 70 wt%, from about 70 wt% to about 99 wt%, from about 70 wt% to about 95 wt%, from about 70 wt% to about 90 wt%, etc.

Further, the silicon particles may or may not be pure silicon. For example, the silicon particles may be substantially silicon, or may be a silicon alloy. In one embodiment, the silicon alloy comprises silicon as a major component, along with one or more other elements.

As described herein, micron-sized silicon particles can provide good volumetric and gravimetric energy densities, along with good cycle life. In certain embodiments, to obtain the benefits of micron-sized silicon particles (e.g., high energy density) and the benefits of nano-sized silicon particles (e.g., good cycling behavior), the silicon particles may have an average or median particle size in the micron range and a surface that includes nano-sized features. In some embodiments, the silicon particles may have a mean particle diameter (e.g., mean diameter or mean largest dimension) or a median particle diameter (e.g., median diameter or median largest diameter) of from about 0.1 μm to about 30 μm or from about 0.1 μm up to all values of about 30 μm. For example, the silicon particles may have the following average or median particle size: about 0.1 μm to about 20 μm, about 0.5 μm to about 25 μm, about 0.5 μm to about 20 μm, about 0.5 μm to about 15 μm, about 0.5 μm to about 10 μm, about 0.5 μm to about 5 μm, about 0.5 μm to about 2 μm, about 1 μm to about 20 μm, about 1 μm to about 15 μm, about 1 μm to about 10 μm, about 5 μm to about 20 μm, and the like. Thus, the average or median particle diameter may be any value from about 0.1 μm to about 30 μm, for example, 0.1 μm, 0.5 μm, 1 μm, 5 μm, 6 μm, 7 μm, 8 μm, 9 μm, 10 μm, 15 μm, 20 μm, 25 μm, and 30 μm.

The nano-sized features may include the following average feature sizes (e.g., average diameter or average largest dimension): about 1nm to about 1 μm, about 1nm to about 750nm, about 1nm to about 500nm, about 1nm to about 250nm, about 1nm to about 100nm, about 10nm to about 500nm, about 10nm to about 250nm, about 10nm to about 100nm, about 10nm to about 75nm, or about 10nm to about 50 nm. The features may include silicon.

The amount of carbon obtained from the precursor may be about 50 wt% of the polyamic acid. In certain embodiments, the amount of carbon obtained from the precursor in the composite may be greater than 0 wt% to about 95 wt%, such as about 1 wt% to about 95 wt%, about 1 wt% to about 90 wt%, 1 wt% to about 80 wt%, about 1 wt% to about 70 wt%, about 1 wt% to about 60 wt%, about 1 wt% to about 50 wt%, about 1 wt% to about 40 wt%, about 1 wt% to about 30 wt%, about 5 wt% to about 95 wt%, about 5 wt% to about 90 wt%, about 5 wt% to about 80 wt%, about 5 wt% to about 70 wt%, about 5 wt% to about 60 wt%, about 5 wt% to about 50 wt%, about 5 wt% to about 40 wt%, about 5 wt% to about 30 wt%, about 10 wt% to about 95 wt%, about 10 wt% to about 90 wt%, about 10 wt%, or about 10 wt% to about 80 wt%, From about 10 wt% to about 80 wt%, from about 10 wt% to about 70 wt%, from about 10 wt% to about 60 wt%, from about 10 wt% to about 50 wt%, from about 10 wt% to about 40 wt%, from about 10 wt% to about 30 wt%, from about 10 wt% to about 25 wt%, etc. For example, the amount of carbon obtained from the precursor can be about 1 wt%, about 5 wt%, about 10 wt%, about 15 wt%, about 20 wt%, about 25 wt%, etc., of the precursor.

The carbon from the precursor may be hard carbon. The hard carbon may be carbon that does not convert to graphite even when heated at more than 2800 degrees celsius. The precursor, which melts or flows during pyrolysis, is converted to soft carbon and/or graphite at sufficient temperature and/or pressure. Hard carbon may be chosen because soft carbon precursors can flow and soft carbon and graphite are mechanically weaker than hard carbon. Other possible hard carbon precursors may include phenolic resins, epoxy resins, and other polymers with very high melting points or crosslinks. In some embodiments, the amount of hard carbon in the composite may have a value of greater than 0 wt% to about 95 wt%, such as about 1 wt% to about 95 wt%, about 1 wt% to about 90 wt%, about 1 wt% to about 80 wt%, about 1 wt% to about 70 wt%, about 1 wt% to about 60 wt%, about 1 wt% to about 50 wt%, about 1 wt% to about 40 wt%, about 1 wt% to about 30 wt%, about 5 wt% to about 95 wt%, about 5 wt% to about 90 wt%, about 5 wt% to about 80 wt%, about 5 wt% to about 70 wt%, about 5 wt% to about 60 wt%, about 5 wt% to about 50 wt%, about 5 wt% to about 40 wt%, about 5 wt% to about 30 wt%, about 10 wt% to about 95 wt%, about 10 wt% to about 90 wt%, about 10 wt%, or about 10 wt% to about 90 wt%, From about 10 wt% to about 80 wt%, from about 10 wt% to about 70 wt%, from about 10 wt% to about 60 wt%, from about 10 wt% to about 50 wt%, from about 10 wt% to about 40 wt%, from about 10 wt% to about 30 wt%, from about 10 wt% to about 25 wt%, etc. In some embodiments, the amount of hard carbon in the composite may be about 1 wt%, about 5 wt%, about 10 wt%, about 20 wt%, about 30 wt%, about 40 wt%, about 50 wt%, or greater than about 50 wt%. In certain embodiments, the hard carbon phase is substantially amorphous. In other embodiments, the hard carbon phase is substantially crystalline. In other embodiments, the hard carbon phase comprises amorphous carbon and crystalline carbon. The hard carbon phase may be the matrix phase in the composite. Hard carbon may also be embedded in the pores of the silicon-containing additive. The hard carbon may react with some additives to produce some material at the interface. For example, a silicon carbide layer may be present between the silicon particles and the hard carbon.

In certain embodiments, heating the mixture to the desired pyrolysis temperature may further result in surface modification of the silicon particles present in the mixture. In some embodiments, pyrolysis of the mixture may result in the formation of a surface coating on at least 50% of the silicon particles present in the mixture. In some embodiments, pyrolysis of the mixture can result in the formation of a surface coating on at least 60%, 70%, 80%, 90%, or 99% of the silicon particles present in the mixture. In some embodiments, the surface coating forms a substantially continuous layer on the silicon particles.

In some embodiments, the carbonized precursor or resin may contact the surface of the silicon particles. In certain embodiments, the carbonized precursor in contact with the surface of the silicon particles may be one or more types of carbon phases resulting from pyrolysis of the precursor. One or more types of carbon phases of the carbonized precursor in contact with the surface of the silicon particles may react with the silicon particles during pyrolysis to form silicon carbide on the surface of the silicon particles. Thus, in some embodiments, the surface coating may comprise carbon, silicon carbide, and/or a mixture of carbon and silicon carbide.

In some embodiments, as described further below, the silicon particles present in the mixture may include natural silicon oxides (SiO )₂、SiO_x) A surface layer. In certain embodiments, the carbonized precursor in contact with the surface of the silicon particles may react with a naturally occurring surface layer of natural silicon oxide to form silicon carbide. In some embodiments, the carbonized precursor in contact with the surface of the silicon particles may react with substantially all of the native silicon oxide layer to form silicon carbide. Thus, in some embodiments, the surface coating on the silicon particles may comprise carbon and silicon carbide, wherein the surface coating is substantially free of silicon oxide. In some casesIn embodiments, the first portion of the surface coating may comprise silicon carbide and the second portion may comprise a mixture of silicon carbide and carbon. In some other embodiments, the carbonized precursor in contact with the surface of the silicon particles may incompletely convert the native silicon oxide layer to silicon carbide, and the resulting surface coating or coatings may comprise carbon, silicon carbide, and one or more silicon oxides, e.g., SiO₂And SiO_x. In some embodiments, the carbonized precursor in contact with the surface of the silicon particles may be fully reacted to obtain a surface coating comprising silicon carbide. In some embodiments, substantially all of the surface coating may comprise silicon carbide. In some embodiments, such surface coatings may be substantially free of silicon oxide and/or carbon.

In certain embodiments, the pyrolyzed mixture may include silicon particles having a surface coating of carbon and/or silicon carbide resulting in a silicon-carbon-silicon carbide composite (e.g., at least one first phase comprising silicon, at least one second phase comprising carbon, and at least one third phase comprising silicon carbide) or a silicon-carbon-silicon carbide composite (e.g., at least one first phase comprising silicon, at least one second phase comprising carbon, at least one third phase comprising carbon, and at least one fourth phase comprising silicon carbide).

In addition, the surface coating on the silicon particles described herein can help limit the outward expansion of the silicon particles during lithiation. By limiting outward particle expansion during lithiation, the surface coating can help prevent mechanical failure of the silicon particles and ensure good electrical contact. The surface coating may further enhance charge transfer within the electrode. The controlled and optimized surface modification of the silicon particles in the anode can also significantly improve the capacity retention during cycling of the associated cell.

In addition, the surface coating substantially affects the reactions that occur between the anode material and the electrolyte within the cell. The surface coating may help reduce unwanted reactions. During pyrolysis, the surface coating formed and the removal of unwanted native oxides (SiO) via conversion to more stable and non-reactive SiC₂) Can provide higherThe irreversible capacity loss is minimized. The irreversible capacity loss may be due to the formation and accumulation of a lithium consuming Solid Electrolyte Interface (SEI) layer. For silicon particles, this becomes a more prominent problem because nanoscale and microscale silicon particles have large surface areas, and larger silicon particles tend to pulverize during lithiation and delithiation, which can introduce additional particle surface area. In addition, the irreversible capacity loss may be due to the reaction of lithium with undesired natural silicon oxides (equation 1), which is unavoidable during processing and storage of the silicon anode material.

SiO_x+yLi+ye→Si+Li_yO_x(reaction formula 1)

Thus, surface modification of the silicon particles by carbon and/or silicon carbide may help to form a relatively stable solid electrolyte interfacial layer, and may reduce or eliminate unwanted reactions of lithium with natural silicon oxides on the surface of the Si particles (equation 1).

Fig. 1B is a schematic illustration of the formation of silicon carbide on silicon particles as described above. First, silicon particles comprising a surface layer of natural silicon oxide are provided in a mixture comprising precursors as described above. In some embodiments, the mixture is pyrolyzed in a reducing atmosphere. For example, a reducing atmosphere, vacuum and/or flowing gas, including H, may be used₂CO or a hydrocarbon gas. In some embodiments, the mixture is heated to about 500 ℃ to about 1350 ℃. In some embodiments, the mixture is heated to about 800 ℃ to about 1200 ℃. In some embodiments, the mixture is heated to about 1175 ℃.

The pyrolyzed precursor in contact with the surface of the silicon particles reacts with the natural silicon oxide layer of the silicon particles to form silicon carbide. The carbonized precursor in contact with the surface of the silicon particles is described herein as being continuous and conformable, but in some other embodiments may not be continuous or conformable. Further, in some embodiments, the silicon carbide layer formed from the reaction between the native silicon oxide layer and the carbonized precursor contacting the surface of the silicon particles may take the form of a coating or dispersion within the composite anode film. As shown in fig. 1B, in some embodiments, the silicon carbide may not be continuous or conformal on the silicon particles, while in some other embodiments, the silicon carbide may be a continuous and/or conformal coating.

In certain embodiments, graphite particles are added to the mixture. Advantageously, graphite may be the electrochemically active material in the cell as well as the elastically deformable material that may respond to the volume change of the silicon particles. Graphite is a preferred active anode material for certain types of lithium ion batteries currently on the market because of its low irreversible capacity. Furthermore, graphite is softer than hard carbon and can better absorb the volume expansion of the silicon additive. In certain embodiments, the particle size (e.g., diameter or largest dimension) of the graphite particles may be from about 0.5 microns to about 20 microns. All, substantially all, or at least some of the graphite particles can include a particle size (e.g., diameter or largest dimension) as described herein. In some embodiments, the graphite particles may have a mean or median particle diameter (e.g., diameter or largest dimension) of about 0.5 microns to about 20 microns. In some embodiments, the graphite particles may have a distribution of particle sizes. For example, at least about 95%, at least about 90%, at least about 85%, at least about 80%, at least about 70%, or at least about 60% of the particles can have a particle size as described herein. In certain embodiments, the composite material may include graphite particles in an amount greater than 0% and less than about 80% by weight, including from about 40% to about 75% by weight, from about 5% to about 30% by weight, from about 5% to about 25% by weight, from about 5% to about 20% by weight, from about 5% to about 15% by weight, and the like.

In certain embodiments, conductive particles, which may also be electrochemically active, are added to the mixture. Such particles enable more electrically conductive composites and more mechanically deformable composites that are able to absorb the large volume changes that occur during lithiation and delithiation. In certain embodiments, the conductive particles can have a particle size (e.g., diameter or largest dimension) of about 10 nanometers to about 7 micrometers. All, substantially all, or at least some of the conductive particles can include a particle size (e.g., diameter or largest dimension) as described herein. In some embodiments, the conductive particles can have a mean or median particle diameter (e.g., diameter or largest dimension) of about 10nm to about 7 microns. In some embodiments, the conductive particles may have a distribution of particle sizes. For example, at least about 95%, at least about 90%, at least about 85%, at least about 80%, at least about 70%, or at least about 60% of the particles can have a particle size as described herein.

In certain embodiments, the mixture may comprise conductive particles in an amount greater than 0 wt% up to about 80 wt%. In other embodiments, the composite material may comprise from about 45% to about 80% by weight. The conductive particles may be conductive carbon, including carbon black, carbon fibers, carbon nanofibers, carbon nanotubes, and the like. Many carbons considered to be non-electrochemically active conductive additives become active once pyrolyzed in the polymer matrix. Alternatively, the conductive particles may be a metal or alloy, including copper, nickel, or stainless steel.

In certain embodiments, the electrode may comprise a composite material described herein. For example, the composite material may form a self-supporting monolithic electrode. The pyrolized carbon phase (e.g., hard carbon phase) of the composite material may remain together and structurally support the particles added to the mixture. In certain embodiments, the self-supporting monolithic electrode does not include a separate collector layer and/or other support structure. In some embodiments, the composite and/or electrode does not contain more than trace amounts of polymer remaining after pyrolysis of the precursor. In other embodiments, the composite material and/or the electrode do not comprise a non-conductive binder. The composite material may also include a porosity, for example a volume porosity of about 1% to about 70% or about 5% to about 50%. For example, the porosity may be from about 5% to about 40% volume porosity.

In some embodiments, the composite material may be attached to a current collector. In some embodiments, the composite material may also be formed into a powder. For example, the composite material may be ground into a powder. The composite powder may be used as an active material for an electrode. For example, the composite powder may be deposited on the collector in a manner similar to the preparation of conventional electrode structures as known in the industry.

In certain embodiments, an electrode in a battery or electrochemical cell may comprise a composite material, including a composite material having silicon particles as described herein. For example, the composite material may be used for the anode and/or the cathode. In certain embodiments, the battery is a lithium ion battery. In other embodiments, the battery is a secondary battery, or in other embodiments, the battery is a primary battery.

Furthermore, the full capacity of the composite material may not be employed during use of the battery to improve the life of the battery (e.g., the number of charge and discharge cycles before the battery fails or battery performance drops below usable levels). For example, a composite having about 70 wt% silicon particles, about 20 wt% carbon from the precursor, and about 10 wt% graphite may have a maximum gravimetric capacity of about 3000mAh/g, while a composite may only use up to about 550mAh/g to about 1500 mAh/g. Although the maximum weight capacity of the composite may not be employed, higher capacities than certain lithium ion batteries may still be achieved using the composite at lower capacities. In certain embodiments, the composite material is used at or only at a weight capacity of less than about 70% of the maximum weight capacity of the composite material. For example, the composite material is not used in a weight capacity that exceeds about 70% of the maximum weight capacity of the composite material. In other embodiments, the composite material is used at or only at a weight capacity of less than about 50% of the maximum weight capacity of the composite material or less than about 30% of the maximum weight capacity of the composite material.

Silicon particles

Described herein are silicon particles for battery electrodes (e.g., anode and cathode). Anode electrodes currently used in rechargeable lithium ion batteries typically have a specific capacity (including metal foil current collectors, conductive additives, and binder materials) of about 200 milliamp hours per gram. The active material graphite used in most lithium ion battery anodes has a theoretical energy density of 372 milliampere hours per gram (mAh/g). In contrast, silicon has a high theoretical capacity of 4200 mAh/g. However, upon lithium intercalation, silicon expands by more than 300%. Due to this expansion, an anode comprising silicon should be able to expand while allowing the silicon to maintain electrical contact with the silicon.

Some embodiments provide silicon particles that can be used as electrochemically active materials in electrodes. In addition to the silicon particles, the electrode may comprise a binder and/or other electrochemically active material. For example, the silicon particles described herein may be used as silicon particles in the composite materials described herein. In another example, the electrode may have a layer of electrochemically active material on the current collector, and the layer of electrochemically active material comprises silicon particles. The electrochemically active material may also comprise one or more types of carbon.

Advantageously, the silicon particles described herein may improve the performance of the electrochemically active material, for example, improve capacity and/or cycling performance. Furthermore, electrochemically active materials having such silicon particles may not be significantly degraded by lithiation of the silicon particles.

In certain embodiments, the silicon particles may have an average particle size, e.g., an average diameter or average largest dimension, of from about 10nm to about 40 μm, as described herein. Other embodiments may include average particle sizes of about 1 μm to about 15 μm, about 10nm to about 1 μm, and about 100nm to about 10 μm. Silicon particles of various sizes may be separated by various methods, such as by air classification, sieving, or other screening methods. For example, a mesh size of 325 may be used to separate particles having a particle size of less than about 44 μm from particles having a particle size of greater than about 44 μm.

Further, the silicon particles may have a distribution of particle sizes. For example, at least about 90% of the particles may have a particle size, e.g., diameter or largest dimension, of about 10nm to about 40 μm, about 1 μm to about 15 μm, about 10nm to about 1 μm, and/or greater than 200 nm.

In some embodiments, the silicon particles may have an average surface area per unit mass of: about 1m²G to about 100m²G, about 1m²G to about 80m²G, about 1m²G to about 60m²G, about 1m²G to about 50m²G, about 1m²G to about 30m²G, about 1m²G to about 10m²G, about 1m²G to about 5m²G, about 2m²G to about 4m²A/g or less than about 5m²/g。

In certain embodiments, the silicon particles are at least partially crystalline, substantially crystalline, and/or fully crystalline. Furthermore, the silicon particles may be substantially pure silicon.

The silicon particles described herein with respect to some embodiments may generally have a larger average particle size than silicon particles used in conventional electrodes. In some embodiments, the average surface area of the silicon particles described herein may be generally small. Without being bound by any particular theory, the smaller surface area of the silicon particles described herein may help to enhance the performance of the electrochemical cell. A typical rechargeable battery anode of the lithium ion type will contain nano-sized silicon particles. To further increase the capacity of the battery, smaller silicon particles (e.g., silicon particles in the nanometer size range) are used to prepare the electrode active material. In some cases, the silicon particles are ground to reduce the size of the particles. Sometimes milling can produce a rough or scratched particle surface, which also increases the surface area. However, the increased surface area of the silicon particles may actually contribute to the degradation of the electrolyte, which results in an increase in irreversible capacity loss. Fig. 2A and 2B are SEM micrographs of exemplary embodiments of silicon particles milled from larger silicon particles. As shown in the figures, certain embodiments may have a rough surface.

As described herein, certain embodiments include silicon particles having a surface roughness in the nanometer size range, such as micron-sized silicon particles having nanometer-sized features on the surface. Fig. 2C and 2D are SEM micrographs of exemplary embodiments of such silicon particles. Various such silicon particles can have an average particle size (e.g., average diameter or average largest dimension) in the micrometer range (e.g., about 0.1 μm to about 30 μm, as described herein) and a surface comprising nanometer-sized features (e.g., about 1nm to about 1 μm, about 1nm to about 750nm, about 1nm to about 500nm, about 1nm to about 250nm, about 1nm to about 100nm, about 10nm to about 500nm, about 10nm to about 250nm, about 10nm to about 100nm, about 10nm to about 75nm, or about 10nm to about 50nm, as described herein). The features may include silicon.

In comparison to the exemplary embodiments shown in fig. 2A and 2B, silicon particles having a combined micro/nano-sized geometry (e.g., fig. 2C and 2D) may have a higher surface area than milled particles. Thus, the silicon particles to be used may be determined by the desired application and specifications.

Although the silicon particles of certain embodiments have nanometer-sized features on the surface, the total surface area of the particles may be more similar to micron-sized particles than nanometer-sized particles. For example, micron-sized silicon particles (e.g., silicon ground from large particles) typically have a particle size greater than about 0.5m²A ratio of the total of the carbon atoms to the carbon atoms of less than about 2m²Average surface area per unit volume (e.g., measured using Brunauer Emmett Teller (BET) particle surface area) of/g, while nano-sized silicon particles typically have a particle size greater than about 100m²A ratio of the total²Average surface area per unit mass in g. Certain embodiments described herein may have the following average surface area per unit mass: about 1m²G to about 30m²G, about 1m²G to about 25m²G, about 1m²G to about 20m²G, about 1m²G to about 10m²G, about 2m²G to about 30m²G, about 2m²G to about 25m²G, about 2m²G to about 20m²G, about 2m²G to about 10m²G, about 3m²G to about 30m²G, about 3m²G to about 25m²G, about 3m²G to about 20m²G, about 3m²G to about 10m²G (e.g., about 3 m)²G to about 6m²Per g), about 5m²G to about 30m²G, about 5m²G to about 25m²G, about 5m²G to about 20m²G, about 5m²G to about 15m²In g or about 5m²G to about 10m²/g。

Various examples of micron-sized silicon particles having nanometer-sized features may be used to form certain embodiments of the composite materials as described herein. For example, fig. 2E illustrates an example method 200 of forming a composite material of certain embodiments. The method 200 includes providing a plurality of silicon particles (e.g., silicon particles having an average particle size of about 0.1 μm to about 30 μm and a surface including nano-sized features), block 210. The method 200 also includes forming a mixture including a precursor and a plurality of silicon particles, block 220. The method 200 also includes pyrolyzing the precursor (block 230) to convert the precursor into one or more types of carbon phases to form the composite material.

With respect to block 210 of the process 200, silicon having the characteristics described herein may be synthesized as a product or byproduct of a Fluidized Bed Reactor (FBR) process. For example, in the FBR process, useful materials may be grown on silicon seed material. Typically, the particles may be removed from the reactor by gravity. Some fine-grained silicon material may exit the reactor from the top of the reactor or may be deposited on the walls of the reactor. The material (e.g., byproduct material) exiting the top of the reactor or deposited on the walls of the reactor may have nanoscale features on the micron-sized particles. In some such methods, a gas (e.g., a nitrogen carrier gas) may be passed through the silicon material. For example, the silicon material may be a plurality of granular silicon. The gas may pass through the silicon material at a sufficiently high velocity to suspend the solid silicon material and cause it to behave like a fluid. The process may be carried out under an inert atmosphere, for example under nitrogen or argon. In some embodiments, silane gas may also be used, for example, to allow metallic silicon to grow on the surface of the silicon particles. The growth from the vapor phase can impart unique surface characteristics, such as nanometer-sized features, to the silicon particles. Because silicon typically cracks in smooth shapes (e.g., like glass), certain embodiments of silicon particles formed using the FBR process may advantageously achieve small features, such as small features in the nanometer size range, which may not be readily available in some embodiments where the silicon particles are formed by milling from larger silicon particles.

In addition, since the FBR process can be under an inert atmosphere, very high purity particles (e.g., greater than 99.9999%) can be obtained. In some embodiments, a purity of about 99.9999% to about 99.999999% may be obtained. In some embodiments, the FBR process may be similar to the process used in the production of solar grade polysilicon while using 85% less energy than the conventional Siemens process, where polysilicon may be formed as trichlorosilane decomposes and deposits additional silicon material on high purity silicon rods at 1150 ℃. Because nano-sized silicon particles have been shown to enhance cycle life performance in electrochemical cells, micron-sized silicon particles have not been considered for use as electrochemically active materials in electrochemical cells.

For blocks 220 and 230 in the method 200, a mixture is formed comprising a precursor and a plurality of silicon particles, block 220, and the precursor is pyrolyzed, block 230, to convert the precursor into one or more types of carbon phases to form a composite material similar to blocks 101 and 105, respectively, in the method 100 described herein. In some embodiments, pyrolysis (e.g., about 900 ℃ to 1350 ℃) occurs at a temperature below the melting point of silicon (e.g., about 1414 ℃) without affecting the nano-sized characteristics of the silicon particles.

According to certain embodiments described herein, certain micron-sized silicon particles with nano-surface features can achieve high energy densities and can be used in composites and/or electrodes in electrochemical cells to improve performance during cell cycling.

Surface modification of silicon particles

As described herein, silicon particles can be used as an electrochemically active material in an electrode. In some embodiments, silicon particles may be used in a silicon-carbon composite electrode. The electrode may be formed by pyrolyzing a mixture comprising a carbon precursor and silicon particles to convert the carbon precursor to one or more carbon phases to form a composite film, wherein the silicon particles are distributed throughout the composite film. Without being bound by theory, the surface of the silicon particles may be modified to improve wetting of the carbon precursor, thereby improving adhesion to the carbon precursor and reducing the amount of porosity in the silicon-carbon interface. Thus, the silicon-carbon composite electrode may have greater physical strength, greater electrical conductivity, and better cycle performance in a battery.

Fig. 3A schematically illustrates exemplary surface-modified silicon particles 300 that may be used as active materials in, for example, silicon composite electrodes in lithium ion batteries. Exemplary silicon particles 300 include a bulk material 301 and a surface 302. The surface 302 may be modified by silane treatment as will be further described and represented by Si-O-Si bonds on the surface 302. For simplicity, the bonds are illustrated as Si-O-Si-R, but may include other bonds, elements, and/or functional groups.

For simplicity, the silicon particles 300 in fig. 3A are illustrated as having a circular cross-sectional shape, such as spherical or cylindrical particles. However, it should be understood that the "silicon particles" 300 described herein may have any regular or irregular cross-sectional shape and are not limited to spherical or cylindrical particles. The silicon particles 300 may be any size as described herein, for example, having a maximum diameter or size of about 10nm to about 50 μm, having a maximum diameter or size of about 1 μm to about 50 μm, and the like.

With continued reference to fig. 3A, the bulk material 301 may have any of the characteristics of any of the silicon particles described herein. For example, bulk material 301 may or may not be pure silicon. For example, bulk material 301 may be substantially silicon, or may be a silicon alloy (e.g., silicon as a major constituent, along with one or more other elements). In some embodiments, bulk material 301 may be about 90% pure silicon to about 99.9999% pure silicon. In some cases, bulk material 301 may be substantially pure silicon. In some embodiments, the bulk material 301 may be at least partially crystalline, substantially crystalline, and/or fully crystalline. In some cases, surface 302 can include a naturally and/or artificially generated oxide layer (e.g., SiO, etc.)₂SiOx, SiOH). The surface oxidation can be carried out in the presence or absence of water at, for example, about 100 ℃ to about 1200 ℃.

In various embodiments, surface 302 may be modified with one or more silicon-containing organic compounds, e.g., organosilanes. In some cases, the organosilane may react with a naturally and/or artificially generated oxide of silicon. For example, one or more organosilanes can react with silanol groups on silicon surface 302 to form bonds (e.g., Si-O-Si) between the silanol groups and the organosilanes. SiliconeThe alkane may comprise a variety of functional groups including, but not limited to: silanols (R-Si-OH), silyl ethers (R-Si-OR'), silyl chlorides (R-Si-Cl), dialkylaminosilanes (R-Si-NR)₂) Silyl cyanide (R-SiH)₃) And/or cyclic azasilanes.

The "R" region of the organosilane may have one or more functional groups tailored for the particular composition used to prepare the silicon composite electrode. For example, to improve wetting and bonding with polyimide materials, aminoalkyl functional groups such as those present in 3-aminopropyltriethoxysilane, N- (2-aminoethyl) -3-aminopropyltrimethoxysilane (AEAPTMS), or 2, 2-dimethoxy-1, 6-diaza-2-silacyclooctane may be used. The molecular structure of 3-aminopropyltriethoxysilane (silyl ether having amine functionality) is shown below.

The molecular structure of N- (2-aminoethyl) -3-aminopropyltrimethoxysilane (silyl ether with diamine functionality) is shown below.

The molecular structure of 2, 2-dimethoxy-1, 6-diaza-2-silacyclooctane (cyclic azasilane) is shown below.

To improve wetting and bonding with the phenolic resin, an epoxy linker may be used. The molecular structure of an exemplary epoxide linker, 5, 6-epoxyhexyltriethoxysilane (silyl ether with epoxide functionality) is shown below.

For materials containing polycyclic aromatic hydrocarbons (e.g., pitch or tar), organosilanes having aromatic functional groups can be used. An example of such an organosilane is benzyltriethoxysilane (silyl ether with aromatic functionality). The molecular structure is shown below.

In some embodiments, the organosilane may comprise a silyl hydride (R-SiH 3). For example, the molecular mechanism of dodecylsilane is shown below.

In some embodiments, the organosilane may comprise a dialkylaminosilane (R-Si-NR 2). For example, the molecular structure of (N, N-dimethylamino) trimethylsilane is shown below.

In various embodiments, the silane treated silicon particles 300 may include a silicon oxide surface that is reacted with one or more organosilanes. For example, the surface 302 of the silicon particle 300 may include a bond between a surface silanol group and an organosilane. There may be different reaction mechanisms for each type of organosilane. Without being bound by theory, the general principle is that silanol groups on the surface 302 of the silicon particles participate in nucleophilic substitution reactions with organosilanes. In the case of silyl chlorides, the reaction can occur via substitution of the chloride groups, forming new Si-O-Si bonds between the silicon particles and the organosilane, producing HCl as a byproduct. In the case of silyl ethers, the reaction mechanism may include a similar direct substitution reaction, producing an alcohol. Alternatively or additionally, the reaction mechanism may comprise a two-step mechanism comprising 1) hydrolysis of the silyl ether to produce alcohol and silanol, and 2) a condensation reaction between the organic silanol and the particle surface silanol to form new Si-O-Si bonds and water as a by-product. Similar nucleophilic substitution reaction mechanisms can be applied to dialkylaminosilanes (e.g., to produce Si-O-Si and secondary amines), silyl hydrides (e.g., to form hydrogen gas), or cyclic azasilanes (e.g., to rearrange to form linear organosilanes). Multifunctional silyl ethers (e.g., AEAPTMS) or silanols can participate in some amount of polymerization at the silicon surface, as each silanol (or hydrolyzed silyl ether) can condense with another silanol to form Si-O-Si.

Surface modification can be carried out using several different methods. In some examples, the silicon may be suspended in a heated liquid containing a concentration of the organosilane. In some cases, the liquid can be heated to a temperature of about 50 ℃ to about 200 ℃ or any range within that range (e.g., about 50 ℃ to about 100 ℃, about 50 ℃ to about 150 ℃, about 50 ℃ to about 175 ℃, about 75 ℃ to about 200 ℃, about 100 ℃ to about 200 ℃, about 150 ℃ to about 200 ℃, etc.). The process can be used for silyl ethers and silyl chlorides. The liquid may be water, an organic solvent, or a mixture of water and an organic solvent. In some cases, some water may be used for the silyl ether. In some cases, little or substantially no water may be used for the silyl chloride. As another example, silicon may be modified by exposure to organosilane vapor, for example, while spreading into a thin layer in a tray or while stirring in a reactor vessel. Other examples are possible.

The amount of organosilane may be related to the specific surface area of the silicon and/or the specific wetting surface of the organosilane. For example, in some cases, 0.6m²Silicon material with specific surface area of 358m²Specific surface wetting organosilanes/g a ratio of about 1.68g of organosilane per kg of silicon may be used.

As described herein, various examples of silane-treated silicon particles may be used to form certain embodiments of the composite materials as described herein. For example, the composite material may be used in an electrode for use in an electrochemical cell.

Certain embodiments may comprise a composite membrane. The composite film may include any of the examples of composite films described herein. For example, the composite film may have from greater than 0 wt% to about 99 wt% (e.g., from about 50 wt% to about 99 wt%, from about 60 wt% to about 99 wt%, from about 70 wt% to about 99 wt%, from about 75 wt% to about 99 wt%, from about 80 wt% to about 99 wt%, etc.) silicon particles, or from greater than 0 wt% to about 95 wt% (e.g., from about 50 wt% to about 95 wt%, from about 60 wt% to about 95 wt%, from about 70 wt% to about 95 wt%, from about 75 wt% to about 95 wt%, from about 80 wt% to about 95 wt%, etc.) silicon particles. The silicon particles may include surface treated silicon particles and/or a combination of surface treated silicon particles and untreated silicon particles. The treated or untreated silicon particles can include any silicon particles described herein (e.g., silicon particles having an average particle size of about 0.1 μm to about 40 μm, silicon particles having an average particle size of about 1 μm to about 20 μm, micron-sized silicon particles having nano-sized features, etc.).

The organic portion of the organosilane can interact with the carbon precursor via various mechanisms, for example, depending on which organosilane and which precursor are used. For example, an organosilane having a primary amine group (e.g., AEAPTMS) can be reacted with a precursor containing a carboxylic acid group (e.g., polyamic acid) to form an amide bond. Other interactions are also possible. Using the same example of AEAPTMS and polyamic acid (or polyimide), the primary amine group in the organosilane can participate in hydrogen bonding with the carbonyl group in the polyamic acid (or polyimide).

Without being bound by theory, the Si-O-Si bonds may be relatively thermally stable such that at least one Si-O-Si monolayer may remain on the surface of the silicon particles, for example, after pyrolysis at about 900 ℃ to about 1350 ℃. For multifunctional silyl ethers, the Si-O-Si domains may be several layers thick, depending on the reaction conditions. Depending on the composition and conditions, the organic portion of the organosilane can be pyrolyzed in a similar mechanism to the carbon precursor, forming hydrogen, water, carbon monoxide, carbon dioxide, cyanide, and/or carbon.

The composite film may also have one or more types of carbon phases from greater than 0 wt% to about 90 wt%. The one or more types of carbon phases may be substantially continuous phases. In some cases, the continuous phase may hold the composite membrane together. In some embodiments, one or more types of carbon phases may be electrochemically active and/or electrically conductive. In some embodiments, the silicon particles may be dispersed throughout the composite film.

As described herein, the silicon particles may have a surface coating. In some embodiments, the surface coating may cover about 50%, 60%, 70%, 80%, 90%, or 99% of the silicon particles. In some embodiments, the surface coating may be a substantially continuous layer. In some embodiments, the surface coating may comprise silicon monoxide (SiO), silicon dioxide (SiO)₂) And/or silicon oxide (SiO)_x). During pyrolysis, some, substantially all, or all of the silicon oxide on the surface of the silicon particles may be converted to silicon carbide.

In various embodiments, the composite film may include an interfacial region between silicon particles and one or more types of carbon phases. The interface region may comprise silicon, carbon, silicon oxide, silicon carbide, silicon oxycarbide, or mixtures of these materials, with or without dopants. The modified surface of the silicon particles can improve wetting of the carbon precursor, thereby improving adhesion to the carbon precursor and reducing porosity in the silicon-carbon interface. In some embodiments, the interface region may include a porosity of less than or equal to about 30%, 25%, 20%, 15%, 10%, or 5%. Advantageously, by having less porosity, the strength and electrical conductivity of the composite material can be increased. In various embodiments, the composite film may be self-supporting. In some embodiments, the composite film may be attached to a current collector. The composite film may be used as an electrode (e.g., an anode or a cathode).

Fig. 3B illustrates an exemplary method 400 of forming certain embodiments of a composite material. The method 400 may include providing a mixture including a carbon precursor and silane treated silicon particles, block 410. The method 400 may also include pyrolyzing the precursor, e.g., to convert the precursor into one or more types of carbon phases, block 420.

With respect to block 410 of the method 400, silane treated silicon particles may be added to a mixture containing a carbon precursor. The silicon particles may be silane treated using any of the embodiments described herein. In some such embodiments, the carbon precursor can comprise a polymer and a solvent, as described herein. The polymer and solvent may include any of the polymers and solvents described herein.

As described herein, the method 400 may also include various steps, such as casting the mixture onto a substrate, drying the mixture to form a film, removing the film from the substrate, and placing the film in a hot press. With respect to block 420 of method 400, the carbon precursor may be pyrolyzed as described herein to convert the precursor into one or more types of carbon phases. The silicon particles may be dispersed throughout the composite film.

As described herein, silane surface treated silicon particles may have better wetting with polymeric binder solutions and stronger ability to adhere to polymeric materials. Advantageously, the adhesion is able to withstand pyrolysis. In silicon-carbon composites, this may translate into less porosity, higher physical strength, and/or better cycling performance, for example, in lithium ion batteries. Without being bound by theory, the SiO increased by the multifunctional silyl ether₂The domains may create increased SiC domains that may provide additional structural integrity to various embodiments of the silicon composite. In many cases, the addition of an interfacial layer between silicon and carbon does not increase resistance and/or impair electrochemical performance. In addition, Si — O in silane may be reduced to form SiC, which may help reduce Li loss of the SEI layer according to equation 1.

Examples

The following exemplary methods for anode fabrication generally include mixing the components together, casting those components onto a release substrate, drying, curing, removing the substrate, and then pyrolyzing the resulting sample. Typically, N-methyl-2-pyrrolidone (NMP) is used as a solvent to change the viscosity of any mixture and allow it to be cast using the doctor blade method.

Example 1

In example 1, a polyimide liquid precursor (PI 2611 from HD Microsystems corpp., a), graphite particles (SLP 30 from Timcal corpp., a), conductive carbon particles (Super P from Timcal corpp., a) and silicon particles (from Alfa Aesar corpp., a) were mixed together in a weight ratio of 200:55:5:20 for 5 minutes using a Spex 8000D machine. The mixture was then cast on aluminum foil and dried in an oven at 90 ℃ to remove the solvent, e.g., NMP. The curing step is then carried out in a hot press at 200 ℃ for at least 12 hours under negligible pressure. The aluminum foil liner was then removed by etching in a 12.5% HCl solution. The remaining membrane was then rinsed in DI water, dried, and then pyrolyzed under a stream of argon at 1175 ℃ for about 1 hour. The process yielded a composition of 15.8 wt% PI 2611 derived carbon, 57.9 wt% graphite particles, 5.3 wt% carbon from Super P and 21.1 wt% silicon.

The resulting electrode was then tested against a lithium NMC oxide cathode in a pouch cell configuration. A typical cycle chart is shown in fig. 4.

Example 2

In example 2, a 1:9 weight ratio of silicon particles (from EVNANO Advanced Chemical Materials Co., Ltd.) was first mixed with NMP using a Turbula mixer for 1 hour. Then, a polyimide liquid precursor (PI 2611 from HD Microsystems corpp., SLP30 from Timcal corpp.,) and carbon nanofibers (CNF from pyrogram corpp.,) were added to the Si: NMP mixture in a weight ratio of 200:55:5:200 and vortexed for about 2 minutes. The mixture was then cast on an aluminum foil covered with a 21 μm thick copper mesh. The sample is then dried in an oven at 90 ℃ to remove the solvent, e.g., NMP. The curing step is then carried out in a hot press at 200 ℃ for at least 12 hours under negligible pressure. The aluminum foil liner was then removed by etching in a 12.5% HCl solution. The remaining film was then rinsed in DI water, dried, and then pyrolyzed under argon at 1000 ℃ for about 1 hour. The method yielded a composition of 15.8 wt% PI 2611 derived carbon, 57.9 wt% graphite particles, 5.3 wt% CNF and 21.1 wt% silicon.

The resulting electrode was then tested against a lithium NMC oxide cathode in a pouch cell configuration. A typical cycle chart is shown in fig. 5.

Example 3

In example 3, a polyimide liquid precursor (PI 2611 from HD Microsystems corpp.) and 325 mesh silicon particles (from Alfa Aesar corpp.) were mixed together using a Turbula mixer in a weight ratio of 40:1 for a duration of 1 hour. The mixture was then cast on aluminum foil and dried in an oven at 90 ℃ to remove the solvent, e.g., NMP. The curing step is then carried out in a hot press at 200 ℃ for at least 12 hours under negligible pressure. The aluminum foil liner was then removed by etching in a 12.5% HCl solution. The remaining membrane was then rinsed in DI water, dried, and then pyrolyzed under a stream of argon at 1175 ℃ for about 1 hour. The method produces a composition of 75 wt% PI 2611 derived carbon and 25 wt% silicon.

The resulting electrode was then tested against a lithium NMC oxide cathode in a pouch cell configuration. A typical cycle chart is shown in fig. 6.

Example 4

In example 4, silicon particles (from Alfa Aesar corpp.), polyimide liquid precursor (PI 2611 from HD Microsystems corpp.), graphite particles (SLP 30 from Timcal corpp.), milled carbon fibers (from fiber Glast Developments corpp.), carbon nanofibers (CNF from pyrogram corpp.), carbon nanotubes (from ann o Technology Limited), conductive carbon particles (Super P from Timcal corpp.), conductive graphite particles (KS 6 from Timca corpp.) were mixed for 5 minutes in a weight ratio of 20:200:30:8:4:2:1:15 using a vortexer. Then, the mixture was cast on an aluminum foil. The sample is then dried in an oven at 90 ℃ to remove the solvent, e.g., NMP. The curing step is then carried out in a hot press at 200 ℃ for at least 12 hours under negligible pressure. The aluminum foil liner was then removed by etching in a 12.5% HCl solution. The remaining film was then rinsed in DI water, dried, and then pyrolyzed under argon at 1175 ℃ for about 1 hour. The process produced a composition similar to the initial mixture, but with 7.5% of the PI 2611 derived carbon moieties by initial weight of the polyimide precursor.

The resulting electrode was then tested against a lithium NMC oxide cathode in a pouch cell configuration. A typical cycle chart is shown in fig. 7.

Example 5

In example 5, a polyimide liquid precursor (PI 2611 from HD Microsystems corpp.) and silicon microparticles (from Alfa Aesar corpp.) were mixed together in a weight ratio of 4:1 using a Turbula mixer for a duration of 1 hour. The mixture was then cast on aluminum foil covered with a carbon mask (from Fibre glass Developments Corporation) and allowed to dry in an oven at 90 ℃ to remove the solvent, e.g., NMP. The curing step is then carried out in a hot press at 200 ℃ for at least 12 hours under negligible pressure. The aluminum foil liner was then removed by etching in a 12.5% HCl solution. The remaining membrane was then rinsed in DI water, dried, and then pyrolyzed under a stream of argon at 1175 ℃ for about 1 hour. The method resulted in a composition of approximately 23 wt% PI 2611 derived carbon, 76 wt% silicon, and the weight of the veil was negligible.

The resulting electrode was then tested against a lithium nickel manganese cobalt oxide (NMC) cathode in a pouch cell configuration. A typical cycle chart is shown in fig. 8.

Example 6

In example 6, a polyimide liquid precursor (PI 2611 from HD Microsystems corpp., a), graphite particles (SLP 30 from Timcal corpp., a) and silicon microparticles (from Alfa Aesar corpp., a) were mixed together in a weight ratio of 200:10:70 for 5 minutes using a Spex 8000D machine. Then, the mixture was cast on an aluminum foil and dried in an oven at 90 ℃ to remove the solvent (e.g., NMP). The curing step is carried out in a hot press at 200 ℃ for at least 12 hours at negligible pressure. The aluminum foil liner was then removed by etching in a 12.5% HCl solution. The remaining membrane was then rinsed in DI water, dried, and then pyrolyzed under a stream of argon at 1175 ℃ for about 1 hour. The process yielded a composition of 15.8 wt% PI 2611 derived carbon, 10.5 wt% graphite particles, 73.7 wt% silicon.

The resulting electrode was then tested against a lithium NMC oxide cathode in a pouch cell configuration. The anode was charged to 600mAh/g per cycle and the discharge capacity per cycle was recorded. A typical cycle chart is shown in fig. 9.

Example 7

In example 7, PVDF and silicon particles (from EVNANO Advanced Chemical Materials Co), conductive carbon particles (Super P from Timcal corp., conductive graphite particles (KS 6 from Timcal corp., graphite), graphite particles (SLP 30 from Timcal corp., graphite) and NMP were mixed in a weight ratio of 5:20:1:4:70: 95. Then, the mixture was cast on an aluminum substrate and placed in an oven at 90 ℃ to remove the solvent, e.g., NMP. The resulting electrode was then tested against a lithium NMC oxide cathode in a pouch cell configuration. A typical cycle chart is shown in fig. 10.

Example 8

Several experiments were performed to obtain the effect of the following conditions: the percentage of polyimide-derived carbon (e.g., 2611c) was varied while the percentage of graphite particles (SLP 30 from Timcal corpp.) was reduced and the percentage of silicon particles (from Alfa Aesar corpp.) was maintained at 20 wt.%.

As shown in fig. 11A and 11B, the results show that more graphite and less 2611c are beneficial for battery performance by increasing specific capacity while decreasing irreversible capacity. Minimizing 2611c adversely affects the strength of the resulting anode, so values near 20 wt.% may be preferred as a compromise in one embodiment.

Example 9

Similar to example 8, if 2611c is held at 20 wt.% and the percentage of Si is increased at the expense of graphite particles, the first-cycle discharge capacity of the resulting electrode is increased. Figure 12 shows that higher silicon content can produce better performing anodes.

Example 10

Polyimide sheets 1 mil thick were pyrolyzed and tested according to the procedure in example 1. Reversible capacity and irreversible capacity are plotted as a function of pyrolysis temperature. FIG. 13 shows that in one embodiment, it is preferred to pyrolyze a polyimide sheet (Upilex by UBE corp) at about 1175 ℃.

Additional embodiments

FIG. 14 is a photograph of a 4.3cm by 4.3cm composite anodic film without a metal foil support layer. The composite anodic film had a thickness of about 30 microns and had a composition of about 15.8 wt% PI 2611 derived carbon, about 10.5 wt% graphite particles, and about 73.7 wt% silicon.

Fig. 15 to 20 are Scanning Electron Microscope (SEM) micrographs of the composite anodic film. The composition of the composite anodic film was about 15.8 wt% PI 2611 derived carbon, about 10.5 wt% graphite particles, and about 73.7 wt% silicon. Fig. 15 and 16 show before cycling is performed (the out-of-focus portion is the bottom portion of the anode and the in-focus portion is the cleaved edge of the composite membrane). Fig. 17, 18, and 19 are SEM micrographs of the composite anodic film after cycling for 10 cycles, and 300 cycles, respectively. SEM micrographs show that the silicon did not have any significant pulverization and the anode did not have an excessive layer of solid electrolyte interface/interphase (SEI) built on top of it after cycling. FIG. 20 is an SEM micrograph of a cross section of a composite anodic film.

The measured properties of exemplary silicon particles are described below. These examples are discussed for illustrative purposes, but should not be construed to limit the scope of the disclosed embodiments.

Fig. 21 is an X-ray powder diffraction (XRD) pattern of sample silicon particles. The XRD patterns indicate that the sample silicon particles are essentially crystalline or polycrystalline in nature.

Fig. 22 to 25 are Scanning Electron Microscope (SEM) micrographs of sample silicon particles. Although SEM micrographs appear to show that the silicon particles may have an average particle size that is larger than the measured flat particle size of about 300nm, without being bound by theory, the particles are believed to have agglomerated together, appearing as larger particles.

Fig. 26 is a chemical analysis of sample silicon particles. Chemical analysis showed that the silicon particles were essentially pure silicon.

Fig. 27A and 27B are exemplary particle size histograms for two micron-sized silicon particles with nanometer-sized features. Granules were prepared by the FBR process. Exemplary silicon particles may have a particle size distribution. For example, at least 90% of the particles can have a particle size, such as a diameter or largest dimension, of about 5 μm to about 20 μm (e.g., about 6 μm to about 19 μm). At least about 50% of the particles may have a particle size of about 1 μm to about 10 μm (e.g., about 2 μm and about 9 μm). Further, at least about 10% of the particles can have a particle size of about 0.5 μm to about 2 μm (e.g., about 0.9 μm and 1.1 μm).

Fig. 28 is a graph comparing the discharge capacity of two types of exemplary silicon particles during battery cycling. The performance of four silicon particle (micron-sized particles with nanometer-sized features) samples prepared by the FBR process was compared to five silicon particle samples prepared by milling larger silicon particles. Thus, certain embodiments of silicon particles having a combined micro/nano-geometry (e.g., prepared by the FBR process) may have enhanced performance relative to various other embodiments of silicon particles (e.g., micron-sized silicon particles prepared by milling larger silicon particles). The type of silicon particles to be used may be tailored to the intended or desired application and specification.

Examples of silane treated silicon particles

In one example, 50g of silicon powder is added to a 1% aqueous solution of 3-aminopropyltriethoxysilane. The mixture was stirred and allowed to react for 5 minutes at room temperature. The treated silicon was then filtered using filter paper and a buchner funnel, rinsed with water, and vacuum dried for 66 hours. The resulting material was mixed with polyamic acid resin, graphite, and N-methyl-pyrrolidone (NMP) into a slurry and coated on a polyethylene terephthalate (PET) substrate. The resulting "green" silicon composite film was removed from the PET, evaluated, and found to have a 60% higher tensile strength than a film made in the same manner using untreated silicon.

In another example, silicon is added to a 2% aqueous solution of N- (2-aminoethyl) -3-aminopropyltrimethoxysilane, refluxed at 100 ℃ for 2 hours, and dried at 200 ℃ for 16 hours. The resulting filter cake was pulverized and analyzed by X-ray photoelectron spectroscopy (XPS) to confirm that the surface had been modified with an organosilane.

In another example, silicon was placed in a glass container and combined with N- (2-aminoethyl) -3-aminopropyltrimethoxysilane, where the compositional weight ratio of organosilane to silicon was 0.4%. The material was stirred at 90 ℃ for 4 hours at atmospheric pressure. This produces a loosely agglomerated powder.

Fig. 29 shows the region of the X-ray photoelectron spectroscopy (XPS) spectra of the silane treated silicon sample and the untreated silicon sample. The spectra of the examples treated in water (with and without silane) are shown as "mosisture processed" and the spectra of the examples placed in a glass container at atmospheric pressure (with or without silane) are shown as "Rotovap processed". The spectra show an increase in the carbon content of the silane treated silicon. In fig. 29, rotovap processed silane treated silicon has a higher peak value than moiure processed silane treated silicon. Without being bound by theory, rotovap processing is performed in a closed vessel at 90 ℃, where silane vapors do not escape, thereby increasing the likelihood of reaction with silicon.

Silane treated silicon (both metal processed and rotocap processed) was milled in NMP with zirconia media and mixed in a slurry containing NMP, graphite and polyamic acid resin. The slurry was then poured at 4.27mg/cm²A loading of (with 15% solvent content) was coated on PET film and densified using a calender. The green embryonic film was then removed from the PET, cut into pieces, and vacuum dried using a two-stage process (120 ℃ for 15h, 220 ℃ for 5 h). The dried film is heat treated at 1175 ℃ to convert the polymer matrix to carbon. SheetSeparately, a 15 μm thick copper foil (applied as 6 wt% varnish in NMP, vacuum dried at 110 ℃ for 16 hours) was coated with polyamide-imide. The silicon-carbon composite film was laminated to the coated copper using a heated hydraulic press (50 seconds, 300 ℃, 4000psi) to form the final silicon-carbon composite electrode. And detecting and analyzing the silicon-carbon composite electrode.

Fig. 30A is a scanning electron microscope (SEM-FIB) micrograph with a focused ion beam of a cross-section of an exemplary silicon-carbon composite made with untreated silicon particles. Fig. 30B is an SEM-FIB micrograph of a cross-section of an exemplary silicon-carbon composite made with silane-treated silicon particles. Composites made with silane treated silicon have less porosity in the silicon-carbon interface region than composites made with untreated silicon.

In another example, silicon is added to a 2.5% solution of N- (2-aminoethyl) -3-aminopropyltrimethoxysilane in N-methyl-2-pyrrolidone and milled with zirconia media for 6 hours. The resulting slurry was mixed with graphite and a polyamic acid resin, and coated on a PET substrate. The film was converted to a silicon-carbon composite electrode following the procedure described above.

The silicon-carbon composite electrode is assembled into a lithium ion battery comprising a cathode, a separator, and an electrolyte solution. The cathode was coated with 23mg/cm²3.02g/cc of a 15 μm aluminum foil containing a film of 95% NCM622, 2.5% conductive carbon additive and 2.5% PVdF. The separator was a 16 μm porous polypropylene film coated with a 3.5 μm thick film consisting of a mixture of PVdF and PMMA. The electrolyte solution included 1.2MLiPF6 in organic carbonate. The cell design has a nominal capacity of 710 mAh. The cells were tested using a constant current/constant voltage charge curve and a constant current discharge curve. The upper voltage limit is 4.1V and the lower voltage limit is 2.75V. The current of the charging step was 1.42A, in which the current limit of the constant voltage part was 0.035A, and the current of the discharging step was 0.35A. Characterization cycles were performed every 50 cycles with a charge current of 0.35A and a discharge current of 0.14A.

Fig. 31 shows a graph of capacity retention versus cycle number for a full cell containing silane treated silicon particles compared to a full cell containing untreated silicon particles. The results for the full cell fabricated with the metal processed and rotovap processed silane processed silicon are shown as "silane processed Si". The results of full cells made with other silane treatments (e.g., addition of organosilane in the slurry) are shown as "directly added silane". Two different organosilane (N- (2-aminoethyl) -3-aminopropyltrimethoxysilane) treatment conditions provided improved capacity retention relative to untreated silicon, tested in full cells at 4.1V to 2.75V versus NCM 622.

Fig. 32 shows a plot of capacity retention versus cycle number for full cells containing silane-treated silicon particles (using the method of adding organosilane in the slurry) compared to full cells containing untreated silicon particles in subsequent experiments. The results demonstrate the improved performance of organosilane treated silicon under slightly altered test conditions (upper voltage cut-off of 4.2V instead of 4.1V and characterization cycles performed every 100 cycles).

Various embodiments have been described above. While the invention has been described with reference to these specific embodiments, the description is intended to be illustrative, and not restrictive. Various modifications and applications may occur to those skilled in the art without departing from the true spirit and scope of the invention as defined in the appended claims.

Claims

1. A method of forming a composite film, the method comprising:

providing a mixture comprising a precursor and silane-treated silicon particles; and

pyrolyzing the mixture to convert the precursor to one or more carbon phases to form the composite film, wherein the silicon particles are distributed throughout the composite film.

2. The method of claim 1, wherein the silane-treated silicon particles comprise silicon particles treated with one or more organosilanes.

3. The method of claim 2, wherein the silane treated silicon particles comprise a silicon oxide surface that reacts with the one or more organosilanes.

4. The method of claim 2, wherein the one or more organosilanes comprises one or more silanols, silyl ethers, silyl chlorides, dialkylaminosilanes, silyl hydrides, or cyclic azasilanes.

5. The method of claim 4, wherein the one or more organosilanes comprises one or more aminoalkyl-functional groups.

6. The method of claim 5, wherein the one or more organosilanes comprises 3-aminopropyltriethoxysilane, N- (2-aminoethyl) -3-aminopropyltrimethoxysilane, or 2, 2-dimethoxy-1, 6-diaza-2-silacyclooctane.

7. The method of claim 5, wherein the precursor comprises polyimide.

8. The method of claim 4, wherein the one or more organosilanes comprises an epoxide linker.

9. The method of claim 8, wherein the epoxide linker comprises 5, 6-epoxyhexyltriethoxysilane.

10. The method of claim 8, wherein the precursor comprises a phenolic resin.

11. The method of claim 4, wherein the one or more organosilanes comprises aromatic functional groups.

12. The method of claim 11, wherein the one or more organosilanes comprises benzyltriethoxysilane.

13. The method of claim 11, wherein the precursor comprises a polycyclic aromatic hydrocarbon.

14. The method of claim 4, wherein the one or more organosilanes comprises dodecyl silane.

15. The method of claim 4, wherein the one or more organosilanes comprises (N, N-dimethylamino) trimethylsilane.

16. The method of claim 2, wherein the silicon particles are suspended in a liquid comprising the one or more organosilanes.

17. The method of claim 2, wherein the silicon particles are exposed to one or more organosilane vapors.

18. The method of claim 2, wherein the mixture comprises the one or more organosilanes.

19. The method of claim 1, wherein the composite film comprises from about 50 wt% to about 99 wt% of the silicon particles.

20. The method of claim 1, wherein the composite film is electrochemically active.

21. The method of claim 1, wherein at least one of the one or more types of carbon phases is a continuous phase that maintains the composite film.

22. A method of forming a battery electrode, wherein the electrode comprises the composite film of claim 1.

23. The method of claim 22, wherein the electrode is an anode.